CN103333997B - Annealing heat treatment method of H13 die steel - Google Patents
Annealing heat treatment method of H13 die steel Download PDFInfo
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Abstract
The invention discloses an annealing heat treatment method of H13 die steel. The method comprises the following steps of: cooling a forged H13 die to 480-520 DEG C by using air; heating the H13 die in a heat treatment furnace to 530-570 DEG C along with the furnace; preserving heat for 3-5 hours so that the die temperature is uniform; after the first-stage heat treatment and the second-stage heat treatment, cooling to 350-400 DEG C along with the furnace; and discharging and performing air cooling to finish the heat treatment. The method disclosed by the invention improves the carbide spheroidization rate which can exceed 95%; and moreover, the carbide distribution is uniform and fine, and the segregation of alloy elements is improved so that the die hardness of the die is more uniform.
Description
Technical field
The invention belongs to heat treating method, specifically refer to a kind of annealing heat treating method of H13 die steel.
Technical background
Alloying element content in H13 die steel reaches 8% left and right, the interpolation of a large amount of alloying elements moves to left eutectoid point, H13 die steel belongs to hypereutectoid steel, the macrosegregation of carbon and alloying element, the particularly effect of chromium, v element, makes this steel in process of setting, occur unbalanced substable eutectic carbide.There is thick eutectic carbides and component segregation in the H13 die steel annealed state core structure of at present a lot of domestic productions, proeutectoid carbide is gathered in grain boundaries, and be linked to be chain-like carbide in local area, and eutectic carbides and proeutectoid carbide are assembled on the impact toughness impact of module at crystal boundary very large.
Due to conventional carbide annealing process, because of Heating temperature lower (860 DEG C of left and right), be difficult to improve form, distribution and the inhomogeneity of structure of carbide, especially large-sized module.Before conventional thermal treatment, increase normalizing treatment one time, can reduce undissolved carbide quantity in steel, refine austenite crystal grain, alleviates the ununiformity of distribution of carbides, improves intensity and toughness.But in the thermal treatment process of current this normalizing+Spheroidizing Annealing, temperature relatively low (960 ~ 980 DEG C), the soaking time shorter (2h) of normalizing heating, the segregation of alloying element can not fully improve, carbide can not be dissolved in austenite fully,, therefore in tissue, there is the problems such as segregation and nodularization rate are low in carbide nodularization fully while causing spheroidizing.
Summary of the invention
The object of this invention is to provide a kind of annealing heat treating method of H13 die steel, the method has improved the nodularization rate of carbide, has reduced the segregation of alloying element in tissue.
For achieving the above object, the annealing heat treating method of the designed H13 die steel of the present invention, comprises the following steps:
1) by H13 module air cooling to 480 ~ 520 DEG C after forging, this temperature, more than martensite point, in case produce martensitic transformation, is then put into heat treatment furnace, is warming up to 530 ~ 570 DEG C with stove, and insulation 3 ~ 5h, makes module temperature even;
2) thermal treatment of first stage: furnace temperature is risen to 1000 ~ 1040 DEG C, insulation 8 ~ 10h, carrying out long insulation at high temperature can be conducive to carbide and melt in austenite, be conducive to the diffusion of alloying element, reach the effect that improves segregation, module is taken out in stove, cold by abrupt wind speed, make module temperature be cooled to 350 ~ 450 DEG C, this temperature is more than martensite point, alloying element is evenly distributed on matrix, and air-cooled being conducive to forms tiny carbide particle and matrix rapidly, breaks carbide network;
3) again by step 2) in cooling H13 module put in heat treatment furnace, controlling rate of heating makes H13 module be heated to 630 ~ 680 DEG C, insulation 3 ~ 5h, avoids in follow-up heat-processed, due to heart portion and surperficial excessive temperature differentials, causing thermal stresses and structural stress;
4) thermal treatment of subordinate phase: step 3) H13 module is heated to 810 ~ 830 DEG C with heat treatment furnace, insulation 10 ~ 15h, make the further nodularization of carbide complete, control heat treatment furnace is cooling and make H13 module be cooled to 630 ~ 670 DEG C, insulation 3 ~ 5h, makes heart portion and surperficial temperature uniformity, cools to 350 ~ 400 DEG C with the furnace, the air cooling of coming out of the stove, completes thermal treatment.
Further, in described step 1), furnace temperature≤300 DEG C of heat treatment furnace.
Again further, in described step 4), heat treatment furnace speed of cooling is 5 ~ 30 DEG C/h.
Advantage of the present invention is as follows:
The present invention is by H13 module air cooling to 480 ~ 520 DEG C after forging, and this temperature is more than martensite point, in case produce martensitic transformation; Normalizing temperature is brought up to 1000 ~ 1040 DEG C, and this is conducive to, and carbide melts in austenite, the diffusion of alloying element, has improved the segregation of alloying element, and liquation carbide is melted fully.The type of cooling that normalizing adopts, for air-cooled rapidly, can make the carbide melting separate out fast and not grow up, and is evenly distributed on matrix, the carbide of separating out is tiny, breaks netted and carbide chain, and alloying element has little time diffusion, segregation is significantly improved, and organizes and has also obtained refinement.In Spheroidizing Annealing process subsequently, nodularization on the tiny uniform carbide of carbide after normalizing, because the carbide after normalizing is tiny, even, the efficiency of Spheroidizing Annealing and nodularization rate are high, nodularization rate can reach more than 95%, and tissue is what to change at the tissue of normalizing, and the tissue after annealing will be more tiny.
Brief description of the drawings
Fig. 1 is thermal treatment process figure of the present invention;
The high power metallographic structure figure that Fig. 2 obtains for thermal treatment process of the present invention, its tissue can reach the above rank of AS3 of North America transfer mold Metallographic standard.
In figure, air cooling to 480 ~ 520 DEG C after 1. forging; 2. interior 530 ~ 570 DEG C of stove, samming 3 ~ 5h; 3. heat-up rate≤100 DEG C in stove/h; 4. interior 1000 ~ 1040 DEG C of stove, insulation 8 ~ 10h; 5. take out module, the cold or spray cooling of strong wind speed makes module be cooled to 350 ~ 450 DEG C of the above temperature of martensite point; 6. module is put into the heat treatment furnace that rises in advance 400 DEG C;
7. control in stove heat-up rate≤100 DEG C/h; 8. interior 630 ~ 680 DEG C of stove, insulation 3 ~ 5h; 9. control in stove heat-up rate≤100 DEG C/h; 10. interior 810 ~ 830 DEG C of stove, insulation 10 ~ 15h;
11. control in stoves speed of cooling≤30 DEG C/h; Interior 630 ~ 670 DEG C of 12. stoves, insulation 3 ~ 5h; 13. cool to 350 ~ 400 DEG C with the furnace, the air cooling of coming out of the stove.
Embodiment
Below in conjunction with specific embodiment, the annealing heat treating method of H13 die steel of the present invention is described in further detail.
Embodiment 1
The H13 module of selecting the φ 500 × 2500mm after forging, concrete thermal treatment process is as follows:
1) by the H13 module air cooling to 500 DEG C after forging, then put into furnace temperature and be the heat treatment furnace of 270 DEG C, be warming up to 550 DEG C with stove, insulation 3h, makes module temperature even;
2) thermal treatment of first stage: furnace temperature is risen to 1020 DEG C, and insulation 9h, carries out module to take out in stove, cold by abrupt wind speed, makes module be cooled to 400 DEG C of the temperature of martensite point;
3) again by step 2) in cooling H13 module put in heat treatment furnace, control rate of heating make H13 module be heated to 650 DEG C, insulation 4h;
4) thermal treatment of subordinate phase: step 3) H13 module is heated to 820 DEG C with heat treatment furnace, insulation 10h, controlling heat treatment furnace speed of cooling is 30 DEG C/h, make H13 module be cooled to 650 DEG C, insulation 4h, cools to 350 DEG C with the furnace, the air cooling of coming out of the stove, completes thermal treatment.
To the metallographic structure of the H13 module after thermal treatment as shown in Figure 2, in figure, be organized as equally distributed globular carbide on ferrite.
Embodiment 2
The H13 module of selecting the φ 500 × 2500mm after forging, concrete thermal treatment process is as follows:
1) by the H13 module air cooling to 520 DEG C after forging, then put into furnace temperature and be the heat treatment furnace of 300 DEG C, be warming up to 570 DEG C with stove, insulation 5h, makes module temperature even;
2) thermal treatment of first stage: furnace temperature is risen to 1040 DEG C, and insulation 8h, carries out module to take out in stove, cold by abrupt wind speed, makes module be cooled to 450 DEG C of the temperature of martensite point;
3) again by step 2) in cooling H13 module put in heat treatment furnace, control rate of heating make H13 module be heated to 630 DEG C, insulation 5h;
4) thermal treatment of subordinate phase: step 3) H13 module is heated to 830 DEG C with heat treatment furnace, insulation 12h, controlling heat treatment furnace speed of cooling is 5 DEG C/h, makes H13 module be cooled to 630 DEG C, and insulation 5h, cools to 380 DEG C with the furnace, and the air cooling of coming out of the stove, completes thermal treatment.
Embodiment 3
The H13 module of selecting the φ 500 × 2500mm after forging, concrete thermal treatment process is as follows:
1) by the H13 module air cooling to 480 DEG C after forging, then put into furnace temperature and be the heat treatment furnace of 100 DEG C, be warming up to 530 DEG C with stove, insulation 4h, makes module temperature even;
2) thermal treatment of first stage: furnace temperature is risen to 1000 DEG C, and insulation 10h, carries out module to take out in stove, cold by abrupt wind speed, makes module be cooled to 350 DEG C of the temperature of martensite point;
3) again by step 2) in cooling H13 module put in heat treatment furnace, control rate of heating make H13 module be heated to 680 DEG C, insulation 3h;
4) thermal treatment of subordinate phase: step 3) H13 module is heated to 810 DEG C with heat treatment furnace, insulation 15h, controlling heat treatment furnace speed of cooling is 10 DEG C/h, make H13 module be cooled to 670 DEG C, insulation 3h, cools to 400 DEG C with the furnace, the air cooling of coming out of the stove, completes thermal treatment.
Claims (1)
1. an annealing heat treating method for H13 die steel, is characterized in that: comprise the following steps:
1) by H13 module air cooling to 480～520 DEG C after forging, then put into heat treatment furnace, be warming up to 530～570 DEG C with stove, insulation 3～5h, makes module temperature even, wherein, and furnace temperature≤300 DEG C of heat treatment furnace;
2) thermal treatment of first stage: furnace temperature is risen to 1000～1040 DEG C, and insulation 8～10h, carries out module to take out in stove, cold by abrupt wind speed, makes module temperature be cooled to 350～450 DEG C;
3) again by step 2) in cooling H13 module put in heat treatment furnace, control rate of heating make H13 module be heated to 630～680 DEG C, insulation 3～5h;
4) thermal treatment of subordinate phase: step 3) in H13 module be heated to 810～830 DEG C with heat treatment furnace, insulation 10～15h, control heat treatment furnace is cooling and make H13 module be cooled to 630～670 DEG C, insulation 3～5h, cool to 350～400 DEG C with the furnace, the air cooling of coming out of the stove, completes thermal treatment, wherein, heat treatment furnace speed of cooling is 5～30 DEG C/h.
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Families Citing this family (11)
| Publication number | Priority date | Publication date | Assignee | Title |
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| CN103572022B (en) * | 2013-11-07 | 2015-05-13 | 大冶特殊钢股份有限公司 | Heat-treatment method for H13 section steel |
| CN104726659B (en) * | 2015-02-10 | 2017-02-01 | 中原特钢股份有限公司 | Thermal treatment process for improving microscopic coarse grains and microstructures of H13 forged piece |
| CN105414425A (en) * | 2015-11-04 | 2016-03-23 | 武汉重工铸锻有限责任公司 | Forging method capable of eliminating coarse grains in forge piece and obtaining uniform and fine grain structure |
| CN106811580B (en) * | 2017-02-13 | 2018-10-09 | 钢铁研究总院 | A kind of annealing process of H13 hot die steels |
| CN108193023B (en) * | 2017-12-01 | 2020-03-27 | 内蒙古北方重工业集团有限公司 | Method for eliminating network carbide in annealing microstructure of H13 die steel |
| CN108823381B (en) * | 2018-07-12 | 2020-04-07 | 河钢股份有限公司 | Heat treatment process for improving structure uniformity of H13 hot work die steel forging material |
| CN109161668A (en) * | 2018-09-11 | 2019-01-08 | 武钢集团襄阳重型装备材料有限公司 | A kind of H13 steel double-fined treatment technique |
| CN109852777B (en) * | 2019-01-18 | 2021-09-28 | 西华大学 | H13 die steel and heat treatment process thereof |
| CN114908301B (en) | 2019-03-01 | 2023-06-09 | 育材堂（苏州）材料科技有限公司 | Hot work die steel, heat treatment method thereof and hot work die |
| CN111455149A (en) * | 2020-05-11 | 2020-07-28 | 山东邦巨实业有限公司 | Isothermal spheroidizing annealing process for H13 steel |
| CN113718092A (en) * | 2021-08-06 | 2021-11-30 | 山西太钢不锈钢股份有限公司 | Homogenization treatment method of bamboo leaf-shaped annealed tissue |
Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1540001A (en) * | 2003-11-01 | 2004-10-27 | 湖南科技大学 | Isothermal spheroidizing technique for H13 steel |
| CN102206739A (en) * | 2011-05-04 | 2011-10-05 | 上海大学 | Dual-refinement treatment process of hot mould steel structure |
| CN102650020A (en) * | 2012-05-14 | 2012-08-29 | 上海大学 | High-silicon high-manganese type high-thermal stability hot work die steel and thermal treatment process thereof |
| CN103173597A (en) * | 2013-02-28 | 2013-06-26 | 辽宁金钢重型锻造有限公司 | Method for improving optional performances of large H13 steel hot-extrusion mould |
Family Cites Families (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2008202078A (en) * | 2007-02-19 | 2008-09-04 | Daido Steel Co Ltd | Hot-working die steel |
-
2013
- 2013-07-02 CN CN201310273193.3A patent/CN103333997B/en active Active
Patent Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1540001A (en) * | 2003-11-01 | 2004-10-27 | 湖南科技大学 | Isothermal spheroidizing technique for H13 steel |
| CN102206739A (en) * | 2011-05-04 | 2011-10-05 | 上海大学 | Dual-refinement treatment process of hot mould steel structure |
| CN102650020A (en) * | 2012-05-14 | 2012-08-29 | 上海大学 | High-silicon high-manganese type high-thermal stability hot work die steel and thermal treatment process thereof |
| CN103173597A (en) * | 2013-02-28 | 2013-06-26 | 辽宁金钢重型锻造有限公司 | Method for improving optional performances of large H13 steel hot-extrusion mould |
Non-Patent Citations (5)
| Title |
|---|
| H13钢锻后热处理工艺;杜广超;《金属热处理》;20120731;第37卷(第7期);第32-34页 * |
| JP特开2008-202078A 2008.09.04 * |
| 杜广超.H13钢锻后热处理工艺.《金属热处理》.2012,第37卷(第7期),第32-34页. * |
| 顾佳羽等.高温正火对H13钢锻后组织的影响.《金属热处理》.2012,第37卷(第6期),第70-72页. * |
| 高温正火对H13钢锻后组织的影响;顾佳羽等;《金属热处理》;20120630;第37卷(第6期);第71页第2段，第72页左栏第1-2段及图3 * |
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Effective date of registration: 20170308 Address after: 430415 Binjiang Road, Yangluo Development Zone, Hubei, China, No. 1, No. Patentee after: Xiangyang heavy equipment Material Co Ltd Address before: 430080 Wuchang, Hubei Friendship Road, No. A, block, floor 999, 15 Patentee before: Wuhan Iron & Steel (Group) Corp. |